JP2019524986A - Clad steel sheet excellent in strength and formability and method for producing the same - Google Patents
Clad steel sheet excellent in strength and formability and method for producing the same Download PDFInfo
- Publication number
- JP2019524986A JP2019524986A JP2018566818A JP2018566818A JP2019524986A JP 2019524986 A JP2019524986 A JP 2019524986A JP 2018566818 A JP2018566818 A JP 2018566818A JP 2018566818 A JP2018566818 A JP 2018566818A JP 2019524986 A JP2019524986 A JP 2019524986A
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- Prior art keywords
- clad
- strength
- steel sheet
- steel
- formability
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 140
- 239000010959 steel Substances 0.000 title claims abstract description 140
- 238000004519 manufacturing process Methods 0.000 title claims description 39
- 239000000463 material Substances 0.000 claims abstract description 117
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 47
- 229910000617 Mangalloy Inorganic materials 0.000 claims abstract description 33
- 229910000975 Carbon steel Inorganic materials 0.000 claims abstract description 31
- 239000010962 carbon steel Substances 0.000 claims abstract description 30
- 239000011572 manganese Substances 0.000 claims abstract description 28
- 239000012535 impurity Substances 0.000 claims abstract description 24
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 17
- 229910001566 austenite Inorganic materials 0.000 claims description 18
- 229910052757 nitrogen Inorganic materials 0.000 claims description 17
- 238000000137 annealing Methods 0.000 claims description 16
- 229910052758 niobium Inorganic materials 0.000 claims description 16
- 229910052782 aluminium Inorganic materials 0.000 claims description 15
- 229910052750 molybdenum Inorganic materials 0.000 claims description 14
- 238000005096 rolling process Methods 0.000 claims description 14
- 229910052719 titanium Inorganic materials 0.000 claims description 14
- 238000007747 plating Methods 0.000 claims description 13
- 229910052796 boron Inorganic materials 0.000 claims description 12
- 229910052804 chromium Inorganic materials 0.000 claims description 12
- 239000010960 cold rolled steel Substances 0.000 claims description 11
- 229910052698 phosphorus Inorganic materials 0.000 claims description 11
- 238000010438 heat treatment Methods 0.000 claims description 10
- 230000009467 reduction Effects 0.000 claims description 8
- 230000009466 transformation Effects 0.000 claims description 8
- 238000001816 cooling Methods 0.000 claims description 7
- 229910052759 nickel Inorganic materials 0.000 claims description 7
- 229910052720 vanadium Inorganic materials 0.000 claims description 7
- 238000003466 welding Methods 0.000 claims description 7
- 238000005097 cold rolling Methods 0.000 claims description 6
- 229910000859 α-Fe Inorganic materials 0.000 claims description 6
- 238000004804 winding Methods 0.000 claims description 5
- 229910018125 Al-Si Inorganic materials 0.000 claims description 4
- 229910018520 Al—Si Inorganic materials 0.000 claims description 4
- 229910018566 Al—Si—Mg Inorganic materials 0.000 claims description 4
- 229910003023 Mg-Al Inorganic materials 0.000 claims description 4
- 229910009369 Zn Mg Inorganic materials 0.000 claims description 4
- 229910007570 Zn-Al Inorganic materials 0.000 claims description 4
- 229910007573 Zn-Mg Inorganic materials 0.000 claims description 4
- 229910007567 Zn-Ni Inorganic materials 0.000 claims description 4
- 229910007614 Zn—Ni Inorganic materials 0.000 claims description 4
- 229910001563 bainite Inorganic materials 0.000 claims description 4
- 229910052742 iron Inorganic materials 0.000 claims description 4
- 238000005554 pickling Methods 0.000 claims description 4
- 230000000717 retained effect Effects 0.000 claims description 4
- 238000005496 tempering Methods 0.000 claims description 4
- 229910052725 zinc Inorganic materials 0.000 claims description 4
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 22
- 229910052799 carbon Inorganic materials 0.000 description 20
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 19
- 239000010936 titanium Substances 0.000 description 16
- 230000000694 effects Effects 0.000 description 15
- 239000010955 niobium Substances 0.000 description 15
- 239000000203 mixture Substances 0.000 description 13
- 239000011651 chromium Substances 0.000 description 12
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 11
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 11
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 10
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 10
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 9
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 9
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 9
- 229910052710 silicon Inorganic materials 0.000 description 9
- 239000010703 silicon Substances 0.000 description 9
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 8
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 8
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 8
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 8
- 229910045601 alloy Inorganic materials 0.000 description 8
- 239000000956 alloy Substances 0.000 description 8
- 238000000034 method Methods 0.000 description 8
- 239000011733 molybdenum Substances 0.000 description 8
- 239000011574 phosphorus Substances 0.000 description 8
- 229910052717 sulfur Inorganic materials 0.000 description 8
- 239000011593 sulfur Substances 0.000 description 8
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 7
- 239000000047 product Substances 0.000 description 7
- 150000001247 metal acetylides Chemical class 0.000 description 6
- 238000005728 strengthening Methods 0.000 description 6
- 238000005098 hot rolling Methods 0.000 description 5
- 230000008569 process Effects 0.000 description 5
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 5
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 4
- 238000005253 cladding Methods 0.000 description 4
- 238000009864 tensile test Methods 0.000 description 4
- 230000015572 biosynthetic process Effects 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 3
- 239000013078 crystal Substances 0.000 description 3
- 238000013461 design Methods 0.000 description 3
- 238000003475 lamination Methods 0.000 description 3
- 150000004767 nitrides Chemical class 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 238000005204 segregation Methods 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- CURLTUGMZLYLDI-UHFFFAOYSA-N Carbon dioxide Chemical compound O=C=O CURLTUGMZLYLDI-UHFFFAOYSA-N 0.000 description 2
- 238000005266 casting Methods 0.000 description 2
- 239000002131 composite material Substances 0.000 description 2
- 239000010949 copper Substances 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 238000011161 development Methods 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- 238000002360 preparation method Methods 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- CADICXFYUNYKGD-UHFFFAOYSA-N sulfanylidenemanganese Chemical compound [Mn]=S CADICXFYUNYKGD-UHFFFAOYSA-N 0.000 description 2
- 238000010301 surface-oxidation reaction Methods 0.000 description 2
- QIJNJJZPYXGIQM-UHFFFAOYSA-N 1lambda4,2lambda4-dimolybdacyclopropa-1,2,3-triene Chemical compound [Mo]=C=[Mo] QIJNJJZPYXGIQM-UHFFFAOYSA-N 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910039444 MoC Inorganic materials 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 230000033228 biological regulation Effects 0.000 description 1
- 229910002092 carbon dioxide Inorganic materials 0.000 description 1
- 239000001569 carbon dioxide Substances 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 238000004140 cleaning Methods 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 239000000498 cooling water Substances 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 230000003111 delayed effect Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000002347 injection Methods 0.000 description 1
- 239000007924 injection Substances 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 229910000510 noble metal Inorganic materials 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 238000003303 reheating Methods 0.000 description 1
- 238000000926 separation method Methods 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 230000006641 stabilisation Effects 0.000 description 1
- 238000011105 stabilization Methods 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 238000010792 warming Methods 0.000 description 1
- 239000013585 weight reducing agent Substances 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B15/00—Layered products comprising a layer of metal
- B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
- B32B15/011—Layered products comprising a layer of metal all layers being exclusively metallic all layers being formed of iron alloys or steels
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/002—Heat treatment of ferrous alloys containing Cr
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/50—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for welded joints
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
- C23C2/06—Zinc or cadmium or alloys based thereon
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
- C23C2/12—Aluminium or alloys based thereon
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/42—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for armour plate
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Pressure Welding/Diffusion-Bonding (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
本発明の一側面は、母材と、上記母材の両側面に備えられるクラッド材と、を含み、上記母材は、重量%で、C:0.3〜1.4%、Mn:12〜25%、残部Fe及び不可避不純物を含むオーステナイト系高マンガン鋼であり、上記クラッド材は、重量%で、C:0.09〜0.4%、Mn:0.3〜4.5%、残部Fe及び不可避不純物を含むマルテンサイト系炭素鋼である強度及び成形性に優れたクラッド鋼板に関する。One aspect of the present invention includes a base material and a clad material provided on both side surfaces of the base material, wherein the base material is C: 0.3 to 1.4% by weight, Mn: 12 ~ 25%, austenitic high manganese steel containing the balance Fe and inevitable impurities, the clad material is, by weight, C: 0.09-0.4%, Mn: 0.3-4.5%, The present invention relates to a clad steel sheet excellent in strength and formability, which is a martensitic carbon steel containing the remaining Fe and inevitable impurities.
Description
本発明は、強度及び成形性に優れたクラッド鋼板及びその製造方法に関する。より詳細には、プレス成形で自動車の構造部材などに用いることができる強度及び成形性に優れたクラッド鋼板に関する。 The present invention relates to a clad steel plate excellent in strength and formability and a method for producing the same. More specifically, the present invention relates to a clad steel plate excellent in strength and formability that can be used for automobile structural members by press forming.
近年、地球温暖化を低減するための二酸化炭素の規制により、自動車の軽量化が強く求められており、且つ自動車の衝突安全性を向上させるために、自動車用鋼板の高強度化が継続的に行われている。かかる高強度鋼板を製造するために、大部分において低温変態組織を活用することが一般的である。しかし、高強度を達成するために低温変態組織を活用する場合には、引張強度1GPa級以上では20%以上の伸びを確保することが難しく、冷間プレス成形で複雑な形状を有する部品に適用することが難しくなる。そのため、必要な用途に合わせた自由な部品設計が難しいという問題がある。 In recent years, there has been a strong demand for weight reduction of automobiles due to carbon dioxide regulations to reduce global warming, and in order to improve automobile collision safety, the strength of automobile steel sheets has been continuously increased. Has been done. In order to produce such a high-strength steel plate, it is common to use a low temperature transformation structure in most cases. However, when using a low temperature transformation structure in order to achieve high strength, it is difficult to secure an elongation of 20% or more with a tensile strength of 1 GPa or higher, and it is applied to parts having complicated shapes by cold press forming. It becomes difficult to do. Therefore, there is a problem that it is difficult to design a free part according to the required application.
一方、冷間プレス成形で複雑な形状の部品を製作するためにフェライト系極低炭素鋼や低炭素鋼を活用する場合には、要求される成形性は確保することができるものの、引張強度400MPa級を確保することが難しく、要求される強度を確保するために鋼材の厚さを厚くする必要があるため、自動車の軽量化を果たせないという問題がある。 On the other hand, when using ferritic ultra-low carbon steel or low-carbon steel to produce parts with complicated shapes by cold press forming, the required formability can be ensured, but the tensile strength is 400 MPa. It is difficult to secure the grade, and it is necessary to increase the thickness of the steel material in order to ensure the required strength, so that there is a problem that the weight of the automobile cannot be reduced.
一方、特許文献1には、炭素(C)やマンガン(Mn)などのオーステナイト安定化元素を大量に添加して鋼組織をオーステナイト単相に維持し、変形中に発生する双晶を用いて強度及び成形性をともに確保する方法が提示されており、オーステナイト単相組織を確保するために、0.5重量%以上の炭素と15重量%以上のMnを添加することが一般的である。 On the other hand, in Patent Document 1, a large amount of an austenite stabilizing element such as carbon (C) or manganese (Mn) is added to maintain the steel structure in an austenite single phase, and strength is obtained by using twins generated during deformation. In order to secure an austenite single phase structure, 0.5% by weight or more of carbon and 15% by weight or more of Mn are generally added.
しかし、この場合、大量のMn添加によって鋼板の製造コストが増加し、超高強度を確保するには限界があり、Mn酸化物が原因でめっき性を確保することが難しくなるという問題がある。 However, in this case, the production cost of the steel sheet increases due to the addition of a large amount of Mn, and there is a limit to securing ultrahigh strength, and there is a problem that it is difficult to ensure plating properties due to the Mn oxide.
また、目標とする強度及び成形性を満たすように鋼材を開発するために、多くの開発コスト及び時間が投資される必要性がある。 Moreover, in order to develop a steel material to satisfy the target strength and formability, it is necessary to invest a lot of development costs and time.
そこで、強度及び成形性に優れながらも、目標とする強度及び成形性を確保することが容易であり、所望の用途に合った自由な部品の設計が可能であるとともに、めっき性に優れた鋼板の開発が求められているのが実情である。 Therefore, it is easy to ensure the target strength and formability while being excellent in strength and formability, and it is possible to design a free part suitable for the desired application, and it is excellent in plateability The fact is that the development of
本発明の目的は、強度及び成形性に優れたクラッド鋼板及びその製造方法を提供することである。 The objective of this invention is providing the clad steel plate excellent in intensity | strength and a moldability, and its manufacturing method.
一方、本発明の課題は、上述した内容に限定されない。本発明の課題は、本明細書の内容全般から理解されることができ、本発明が属する技術分野において通常の知識を有する者であれば、本発明の追加的な課題を明確に理解するものである。 On the other hand, the subject of this invention is not limited to the content mentioned above. The problems of the present invention can be understood from the entire contents of this specification, and those who have ordinary knowledge in the technical field to which the present invention belongs will clearly understand the additional problems of the present invention. It is.
本発明の一側面は、母材と、上記母材の両側面に備えられるクラッド材と、を含み、上記母材は、重量%で、C:0.3〜1.4%、Mn:12〜25%、残部Fe及び不可避不純物を含むオーステナイト系高マンガン鋼であり、上記クラッド材は、重量%で、C:0.09〜0.4%、Mn:0.3〜4.5%、残部Fe及び不可避不純物を含むマルテンサイト系炭素鋼であることを特徴とする強度及び成形性に優れたクラッド鋼板に関する。 One aspect of the present invention includes a base material and a clad material provided on both side surfaces of the base material, wherein the base material is C: 0.3 to 1.4% by weight, Mn: 12 ~ 25%, austenitic high manganese steel containing the balance Fe and inevitable impurities, the clad material is, by weight, C: 0.09-0.4%, Mn: 0.3-4.5%, The present invention relates to a clad steel plate excellent in strength and formability, which is a martensitic carbon steel containing the remaining Fe and inevitable impurities.
本発明の他の一側面は、重量%で、C:0.3〜1.4%、Mn:12〜25%、残部Fe及び不可避不純物を含むオーステナイト系高マンガン鋼の母材を用意する段階と、重量%で、C:0.09〜0.4%、Mn:0.3〜4.5%、残部Fe及び不可避不純物を含むマルテンサイト系炭素鋼のクラッド材を用意する段階と、二つの上記クラッド材の間に上記母材を配置して積層物を得る段階と、上記積層物の端を溶接した後、1050〜1350℃の温度範囲で加熱する段階と、上記加熱された積層物を750〜1050℃の温度範囲で仕上げ圧延して熱延鋼板を得る段階と、上記熱延鋼板を50〜700℃で巻取る段階と、上記巻取られた熱延鋼板を酸洗した後、冷間圧下率35〜90%を適用して冷間圧延することで冷延鋼板を得る段階と、上記冷延鋼板を550℃以上上記クラッド材のA3+200℃以下の温度範囲で焼鈍する段階と、を含む強度及び成形性に優れたクラッド鋼板の製造方法に関する。 Another aspect of the present invention is a step of preparing a base material of austenitic high manganese steel containing C: 0.3-1.4%, Mn: 12-25%, balance Fe and inevitable impurities in weight%. And a step of preparing a clad material of martensitic carbon steel containing C: 0.09 to 0.4%, Mn: 0.3 to 4.5%, the balance Fe and unavoidable impurities in weight%; Arranging the base material between the two clad materials to obtain a laminate, welding the ends of the laminate and then heating in a temperature range of 1050 to 1350 ° C., and the heated laminate After rolling in a temperature range of 750 to 1050 ° C. to obtain a hot rolled steel sheet, winding the hot rolled steel sheet at 50 to 700 ° C., and pickling the wound hot rolled steel sheet, Cold-rolled steel sheet is obtained by cold rolling with a cold reduction of 35-90% Phase and a process for the preparation of strength and formability excellent clad plate including the steps of annealing at a temperature in the range of A3 + 200 ° C. or less of the cold-rolled steel sheet 550 ° C. or more above the clad material.
なお、上記した課題の解決手段は、本発明の特徴をすべて列挙したものではない。本発明の様々な特徴とそれに伴う利点及び効果は、以下の具体的な実施形態を参照して、より詳細に理解することができる。 Note that the means for solving the problems described above do not enumerate all the features of the present invention. Various features of the present invention and the attendant advantages and advantages can be more fully understood with reference to the following specific embodiments.
本発明によると、降伏強度が700MPa以上、引張強度と伸びの積が25,000MPa%以上であり、成形性に優れるため自動車用の鋼板などに好適に適用することができ、冷間プレス成形を適用できるクラッド鋼板及びその製造方法を提供することができるという効果を奏する。 According to the present invention, the yield strength is 700 MPa or more, the product of tensile strength and elongation is 25,000 MPa% or more, and since it is excellent in formability, it can be suitably applied to automobile steel sheets, etc. It is possible to provide an applicable clad steel plate and a method for producing the same.
以下、本発明の好ましい実施形態を説明する。しかし、本発明の実施形態は、いくつかの他の形態に変形することができ、本発明の範囲が以下に記述する実施形態に限定されるものではない。また、本発明の実施形態は、当該技術分野において平均的な知識を有する者に本発明をさらに完全に説明するために提供されるものである。 Hereinafter, preferred embodiments of the present invention will be described. However, the embodiments of the present invention can be modified into several other forms, and the scope of the present invention is not limited to the embodiments described below. In addition, the embodiments of the present invention are provided to more fully explain the present invention to those skilled in the art.
本発明者らは、従来の高マンガン鋼系鋼板において大量のマンガン及び炭素の添加により、常温で鋼の微細組織をオーステナイトに維持することで成形性の確保が可能であったが、大量の合金元素添加によって製造コストが高くなり、降伏強度が低いため衝突特性が低下するという問題や、めっき性が劣化するという問題があることを認知し、これを解決するために深く研究した。 The inventors have been able to ensure formability by maintaining the microstructure of the steel in austenite at room temperature by adding a large amount of manganese and carbon in a conventional high manganese steel steel sheet, Recognizing that the addition of elements increases the manufacturing cost and the yield strength is low, there is a problem that the impact characteristics are deteriorated and the plating property is deteriorated.
その結果、成形性に優れたオーステナイト系高マンガン鋼を母材とし、強度に優れ、製造コストが低いマルテンサイト系炭素鋼をクラッド材とする複合鋼板を製造することにより優れた強度及び成形性を確保することができ、クラッド材と母材の厚さ比を制御することで、目標とする強度及び成形性が確保しやすくなり、用途に合った自由な部品の設計が可能となるとともに、めっき性に優れるという効果を得ることができる事実を確認し、本発明を完成するに至った。 As a result, excellent strength and formability can be achieved by manufacturing a composite steel sheet using martensitic carbon steel with excellent strength and low manufacturing cost as the base material, austenitic high manganese steel with excellent formability. By controlling the thickness ratio of the clad material and the base material, it becomes easy to ensure the target strength and formability, and it is possible to design free parts suitable for the application, and to perform plating. The fact that the effect of superiority can be obtained has been confirmed, and the present invention has been completed.
「強度及び成形性に優れたクラッド鋼板」
以下、本発明の一側面による強度及び成形性に優れたクラッド鋼板について詳細に説明する。
"Clad steel sheet with excellent strength and formability"
Hereinafter, a clad steel sheet excellent in strength and formability according to one aspect of the present invention will be described in detail.
本発明の一側面による強度及び成形性に優れたクラッド鋼板は、母材と、上記母材の両側面に備えられるクラッド材と、を含み、上記母材は、重量%で、C:0.3〜1.4%、Mn:12〜25%、残部Fe及び不可避不純物を含むオーステナイト系高マンガン鋼であり、上記クラッド材は、重量%で、C:0.09〜0.4%、Mn:0.3〜4.5%、残部Fe及び不可避不純物を含むマルテンサイト系炭素鋼であることを特徴とする。 A clad steel plate excellent in strength and formability according to one aspect of the present invention includes a base material and a clad material provided on both side surfaces of the base material, and the base material is C: 0. 3 to 1.4%, Mn: 12 to 25%, austenitic high manganese steel containing the remainder Fe and inevitable impurities, the clad material is in weight%, C: 0.09 to 0.4%, Mn : 0.3-4.5% martensitic carbon steel containing the balance Fe and inevitable impurities.
以下、本発明の母材及びクラッド材についてそれぞれ説明した後、上記母材の両側面に備えられるクラッド材を含むクラッド鋼板について説明する。 Hereinafter, after describing the base material and the clad material of the present invention, the clad steel plate including the clad material provided on both side surfaces of the base material will be described.
(母材(オーステナイト系高マンガン鋼))
以下、本発明の一側面によるクラッド鋼板の母材を構成するオーステナイト系高マンガン鋼の合金組成について詳細に説明する。ここで、各元素の含有量の単位は、特別な記載がない限り重量%である。
(Base material (Austenitic high manganese steel))
Hereinafter, the alloy composition of the austenitic high manganese steel constituting the base material of the clad steel plate according to one aspect of the present invention will be described in detail. Here, the unit of the content of each element is% by weight unless otherwise specified.
炭素(C):0.3〜1.4%
炭素は、オーステナイト相の安定化に寄与する元素であって、その含有量が増加するほどオーステナイト相を確保するのに有利な側面がある。また、炭素は、鋼の積層欠陥エネルギーを増加させることで、引張強度及び伸びをともに増加させる役割を果たす。かかる炭素の含有量が0.3%未満の場合には、オーステナイト相の安定性を確保するために添加する必要があるMnの量が過大となり製造コストが上昇するという問題があり、引張強度及び伸びを確保することが難しくなるという問題がある。
これに対し、その含有量が1.4%を超えると、電気比抵抗が増加して溶接性が低下するおそれがある。したがって、本発明では、上記炭素の含有量を0.3〜1.4%に制限することが好ましい。
Carbon (C): 0.3-1.4%
Carbon is an element that contributes to stabilization of the austenite phase, and as its content increases, there is an advantageous aspect for securing the austenite phase. Carbon also serves to increase both tensile strength and elongation by increasing the stacking fault energy of steel. When the carbon content is less than 0.3%, there is a problem that the amount of Mn that needs to be added to ensure the stability of the austenite phase is excessive and the production cost is increased, and the tensile strength and There is a problem that it is difficult to ensure the growth.
On the other hand, if the content exceeds 1.4%, the electrical resistivity may increase and the weldability may decrease. Therefore, in the present invention, it is preferable to limit the carbon content to 0.3 to 1.4%.
マンガン(Mn):12〜25%
マンガンは、炭素とともにオーステナイト相を安定化させる元素である。その含有量が12%未満の場合には、変形中にα’−マルテンサイト相が形成されて安定したオーステナイト相を確保することが難しい。これに対し、25%を超えると、本発明の関心事項である強度の増加と関連したさらなる向上が実質的に生じることなく、製造コストが上昇するという問題がある。したがって、本発明において、Mnの含有量は、12〜25%に制限することが好ましい。
Manganese (Mn): 12-25%
Manganese is an element that stabilizes the austenite phase together with carbon. When the content is less than 12%, it is difficult to ensure a stable austenite phase by forming an α′-martensite phase during deformation. On the other hand, if it exceeds 25%, there is a problem that the manufacturing cost increases without further improvement associated with the increase in strength, which is a matter of concern of the present invention. Therefore, in the present invention, the Mn content is preferably limited to 12 to 25%.
上記母材の残りの成分は鉄(Fe)である。但し、通常の製造過程では、原料や周囲の環境から意図しない不純物が必然的に混入される可能性があるため、これを排除することはできない。これらの不純物は、通常の製造過程における技術者であれば誰でも分かるものであるため、そのすべての内容を具体的に言及することはしない。 The remaining component of the base material is iron (Fe). However, in a normal manufacturing process, unintended impurities may be inevitably mixed from the raw materials and the surrounding environment, and thus cannot be excluded. Since these impurities can be understood by any engineer in the normal manufacturing process, the entire contents thereof are not specifically mentioned.
上記組成に加えて、母材を構成するオーステナイト系高マンガン鋼は、重量%で、Si:0.03〜2.0%、Al:0.02〜2.5%、N:0.04%以下(0%は除く)、P:0.03%以下、及びS:0.03%以下をさらに含むことができる。 In addition to the above composition, the austenitic high manganese steel constituting the base material is, by weight, Si: 0.03-2.0%, Al: 0.02-2.5%, N: 0.04% The following may be included (excluding 0%), P: 0.03% or less, and S: 0.03% or less.
シリコン(Si):0.03〜2.0%
シリコンは、固溶強化による鋼の降伏強度及び引張強度を向上させるために添加しうる成分である。シリコンは、脱酸剤として用いられるため、通常、0.03%以上鋼中に含まれることができる。シリコンの含有量が2.0%を超えると、電気比抵抗を増加させて溶接性が劣化するという問題がある。したがって、シリコンの含有量は、0.03〜2.0%に制限することが好ましい。
Silicon (Si): 0.03-2.0%
Silicon is a component that can be added to improve the yield strength and tensile strength of steel by solid solution strengthening. Since silicon is used as a deoxidizer, it can usually be contained in steel in an amount of 0.03% or more. If the silicon content exceeds 2.0%, there is a problem that the electrical resistivity is increased and the weldability is deteriorated. Accordingly, the silicon content is preferably limited to 0.03 to 2.0%.
アルミニウム(Al):0.02〜2.5%
アルミニウムは、通常、鋼の脱酸のために添加する元素である。本発明では、積層欠陥エネルギーを高めてε−マルテンサイトの生成を抑制することにより、鋼の延性及び耐遅延破壊特性を向上させる役割のために添加することができる。
アルミニウムは、溶鋼中に不純物として存在する元素である。0.02%未満に制御するためには過大な費用が発生し、一方で、上記アルミニウム含有量が2.5%を超えると、鋼の引張強度が低下し、鋳造性が劣化するという問題がある。したがって、本発明では、上記アルミニウムの含有量を0.02〜2.5%に制限することが好ましい。
Aluminum (Al): 0.02 to 2.5%
Aluminum is an element usually added for deoxidation of steel. In this invention, it can add for the role which improves the ductility and delayed fracture resistance of steel by raising the stacking fault energy and suppressing the production | generation of (epsilon) -martensite.
Aluminum is an element present as an impurity in molten steel. In order to control to less than 0.02%, an excessive cost occurs. On the other hand, if the aluminum content exceeds 2.5%, the tensile strength of the steel is lowered and the castability is deteriorated. is there. Therefore, in the present invention, it is preferable to limit the aluminum content to 0.02 to 2.5%.
窒素(N):0.04%以下(0%は除く)
窒素(N)は、オーステナイト結晶粒内において凝固過程中にAlと作用して微細な窒化物を析出させ、双晶(Twin)の発生を促進するため、鋼板を成形する際に強度及び延性を向上させる。しかし、その含有量が0.04%を超えると、窒化物が析出しすぎるため熱間加工性及び伸びが低下する可能性がある。したがって、本発明において、上記窒素の含有量は、0.04%以下に制限することが好ましい。
Nitrogen (N): 0.04% or less (excluding 0%)
Nitrogen (N) acts with Al in the austenite grains during the solidification process to precipitate fine nitrides and promotes the generation of twins. Therefore, strength and ductility are reduced when forming a steel sheet. Improve. However, if the content exceeds 0.04%, nitrides are excessively precipitated, which may reduce hot workability and elongation. Therefore, in the present invention, the nitrogen content is preferably limited to 0.04% or less.
リン(P):0.03%以下
リンは、必然的に含まれる不純物であって、偏析によって鋼の加工性を低下させる主な原因となる元素であるため、その含有量をできる限り低く制御することが好ましい。理論上リンの含有量は0%に制限することが有利であるが、製造工程上必然的に含有される。したがって、上限を管理することが重要であり、本発明では、上記リンの含有量の上限を0.03%に管理するとよい。
Phosphorus (P): 0.03% or less Phosphorus is an impurity that is inevitably contained, and is an element that is a main cause of reducing the workability of steel due to segregation, so its content is controlled as low as possible. It is preferable to do. Theoretically, the phosphorus content is advantageously limited to 0%, but is necessarily contained in the production process. Therefore, it is important to manage the upper limit, and in the present invention, the upper limit of the phosphorus content is preferably managed to 0.03%.
硫黄(S):0.03%以下
硫黄は、必然的に含まれる不純物であって、粗大なマンガン硫化物(MnS)を形成してフランジクラックなどの欠陥を発生させ、鋼板の穴拡げ性を大幅に低下させるため、その含有量をできる限り低く制御することが好ましい。理論上硫黄の含有量は0%に制限することが有利であるが、製造工程上必然的に含有される。したがって、上限を管理することが重要であり、本発明において、上記硫黄の含有量の上限は0.03%に管理するとよい。
Sulfur (S): 0.03% or less Sulfur is an impurity that is inevitably contained, and forms coarse manganese sulfide (MnS) to generate defects such as flange cracks, thereby increasing the hole expandability of the steel sheet. In order to reduce significantly, it is preferable to control the content as low as possible. Theoretically, the sulfur content is advantageously limited to 0%, but is necessarily contained in the production process. Therefore, it is important to manage the upper limit, and in the present invention, the upper limit of the sulfur content is preferably managed to 0.03%.
また、上記組成に加えて、母材を構成するオーステナイト系高マンガン鋼は、重量%で、Ti:0.01〜0.5%、B:0.0005〜0.005%、Mo:0.05〜1.0%、Cr:0.2〜3.0%、Nb:0.01〜0.5%、及びV:0.05〜0.7%のうち1以上をさらに含むことができる。 In addition to the above composition, the austenitic high-manganese steel constituting the base material is, by weight, Ti: 0.01 to 0.5%, B: 0.0005 to 0.005%, Mo: 0.00. It may further include one or more of 05 to 1.0%, Cr: 0.2 to 3.0%, Nb: 0.01 to 0.5%, and V: 0.05 to 0.7%. .
チタン(Ti):0.01〜0.5%
チタンは、鋼材内部の窒素と反応して窒化物が沈殿されて、熱間圧延の成形性を向上させる。また、上記チタンは、一部が鋼材の炭素と反応して析出相を形成することで強度を増加させる役割を果たす。このために、チタンは、0.01%以上含まれることが好ましいが、一方で、0.5%を超えると、沈殿物が形成されすぎるため、部品の疲労特性を悪化させることがある。したがって、上記チタンの含有量は、0.01〜0.5%であることが好ましい。
Titanium (Ti): 0.01 to 0.5%
Titanium reacts with nitrogen inside the steel material to precipitate nitrides, thereby improving the hot rolling formability. Further, the titanium plays a role of increasing the strength by partly reacting with carbon of the steel material to form a precipitated phase. For this reason, titanium is preferably contained in an amount of 0.01% or more. On the other hand, if it exceeds 0.5%, a precipitate is formed too much, which may deteriorate the fatigue characteristics of the part. Therefore, the titanium content is preferably 0.01 to 0.5%.
ホウ素(B):0.0005〜0.005%
ホウ素は、微量添加される場合は、鋳片の粒界を強化し、熱間圧延性を向上させる。但し、ホウ素の含有量が0.0005%未満の場合には、上記の効果が十分に現れない。これに対し、ホウ素の含有量が0.005%を超えると、さらなる性能の向上を期待することができず、コストの増加を招く。したがって、ホウ素の含有量は、0.0005〜0.005%であることが好ましい。
Boron (B): 0.0005 to 0.005%
Boron strengthens the grain boundary of the slab and improves hot rollability when added in a trace amount. However, when the boron content is less than 0.0005%, the above effect is not sufficiently exhibited. On the other hand, if the boron content exceeds 0.005%, further performance improvement cannot be expected, resulting in an increase in cost. Therefore, the boron content is preferably 0.0005 to 0.005%.
クロム(Cr):0.2〜3.0%
クロムは、強度を増加させる効果的な元素である。かかる効果を得るために、クロムの含有量が0.2%以上であることが好ましい。これに対し、上記クロムの含有量が3.0%を超えると、熱間圧延の際に、結晶粒界に粗大な炭化物を形成して熱間加工性を阻害するため、添加量を3.0%以下に限定した。したがって、クロムの含有量は、0.2〜3.0%であることが好ましい。
Chromium (Cr): 0.2-3.0%
Chromium is an effective element that increases strength. In order to obtain such an effect, the chromium content is preferably 0.2% or more. On the other hand, if the chromium content exceeds 3.0%, during hot rolling, coarse carbides are formed at the grain boundaries and hot workability is hindered. Limited to 0% or less. Therefore, the chromium content is preferably 0.2 to 3.0%.
モリブデン(Mo):0.05〜1.0%
モリブデンは、炭素の拡散速度を遅くすることで炭窒化物の粗大化を防止し、析出強化の効果を増大させるために添加することができる。かかる効果を得るためには、上記モリブデンの含有量が0.05重量%以上であることが好ましい。これに対し、モリブデンの含有量が1.0%を超えると、高温でモリブデン炭化物が形成されて鋳片の表面クラックを誘発するという問題がある。したがって、本発明において、上記モリブデンの含有量は、0.05〜1.0%であることが好ましい。
Molybdenum (Mo): 0.05-1.0%
Molybdenum can be added to slow the carbon diffusion rate to prevent coarsening of the carbonitride and increase the effect of precipitation strengthening. In order to obtain such an effect, the molybdenum content is preferably 0.05% by weight or more. On the other hand, if the molybdenum content exceeds 1.0%, molybdenum carbide is formed at a high temperature, which causes a problem of surface cracks in the slab. Therefore, in the present invention, the molybdenum content is preferably 0.05 to 1.0%.
ニオブ(Nb):0.01〜0.5%
ニオブは、炭素と反応して炭化物を形成する元素であって、結晶粒界の微細化及び析出強化により鋼の降伏強度を増加させるために添加することができる。かかる効果を得るためには、上記ニオブの含有量が0.01%以上であることが好ましい。これに対し、ニオブの含有量が0.5%を超えると、高温で粗大な炭化物が形成されて、鋳片の表面クラックを誘発するという問題がある。したがって、本発明において、上記ニオブの含有量は、0.01〜0.5%に制限することが好ましい。
Niobium (Nb): 0.01-0.5%
Niobium is an element that reacts with carbon to form carbides, and can be added to increase the yield strength of steel by refinement of grain boundaries and precipitation strengthening. In order to obtain such an effect, the niobium content is preferably 0.01% or more. On the other hand, when the content of niobium exceeds 0.5%, there is a problem that coarse carbides are formed at a high temperature to induce surface cracks in the slab. Therefore, in the present invention, the niobium content is preferably limited to 0.01 to 0.5%.
バナジウム(V):0.05〜0.7%
バナジウムは、炭素又は窒素と反応して炭窒化物を形成する元素であって、結晶粒度の微細化及び析出強化により降伏強度を増加させるために添加することができる成分である。かかる効果を得るためには、上記バナジウムの含有量が0.05%以上であることが好ましい。これに対し、上記バナジウムの含有量が0.7%を超えると、高温で粗大な炭窒化物が形成されて、熱間加工性が低下するという問題がある。したがって、本発明において、上記バナジウムの含有量は、0.05〜0.7%に制限することが好ましい。
Vanadium (V): 0.05 to 0.7%
Vanadium is an element that forms carbonitride by reacting with carbon or nitrogen, and is a component that can be added to increase the yield strength by refinement of crystal grain size and precipitation strengthening. In order to obtain such an effect, the vanadium content is preferably 0.05% or more. On the other hand, if the vanadium content exceeds 0.7%, coarse carbonitrides are formed at a high temperature, and hot workability is deteriorated. Therefore, in the present invention, the vanadium content is preferably limited to 0.05 to 0.7%.
一方、本発明において、母材を構成するオーステナイト系高マンガン鋼は、上記成分系を満たすだけでなく、鋼板の微細組織として、オーステナイト単相組織を確保することが好ましい。上記のような微細組織を確保することにより、強度及び伸びをともに確保することができる。ここで、オーステナイト単相とは、微細組織が、オーステナイトが95面積%以上であり、残りの炭化物及び不可避不純物の組織からなることを意味する。 On the other hand, in the present invention, it is preferable that the austenitic high-manganese steel constituting the base material not only satisfies the above component system but also ensures an austenitic single-phase structure as the microstructure of the steel sheet. By securing the fine structure as described above, both strength and elongation can be ensured. Here, the austenite single phase means that the microstructure is composed of 95% by area or more of austenite and the structure of the remaining carbides and inevitable impurities.
(クラッド材(マルテンサイト系炭素鋼))
以下、本発明の一側面によるクラッド鋼板のクラッド材を構成するマルテンサイト系炭素鋼の合金組成について詳細に説明する。各元素の含有量の単位は、特別な記載がない限り重量%である。
(Clad material (martensitic carbon steel))
Hereinafter, the alloy composition of the martensitic carbon steel constituting the clad material of the clad steel sheet according to one aspect of the present invention will be described in detail. The unit of the content of each element is% by weight unless otherwise specified.
炭素(C):0.09〜0.4%
炭素は、鋼の硬化能を増加させるとともに、マルテンサイト組織の確保を容易にする元素でありながら、マルテンサイト内で侵入型サイトに位置し、固溶強化により鋼の強度を向上させる元素である。その含有量が0.09%未満の場合には、マルテンサイト変態開始が高温で起こるため、冷却中の炭素が転位に拡散し、固溶強化により鋼の強度を向上させる役割を期待することができない。これに対し、その含有量が0.4%を超えると、鋼板の溶接性を低下するおそれがある。したがって、本発明では、上記炭素の含有量を0.09〜0.4%に制限することが好ましい。
Carbon (C): 0.09 to 0.4%
Carbon is an element that increases the hardenability of steel and facilitates securing a martensite structure, but is located at an interstitial site in martensite and improves the strength of steel by solid solution strengthening. . When the content is less than 0.09%, the start of martensitic transformation occurs at a high temperature, so that the carbon during cooling diffuses into dislocations and can be expected to improve the strength of the steel by solid solution strengthening. Can not. On the other hand, when the content exceeds 0.4%, the weldability of the steel sheet may be reduced. Therefore, in the present invention, it is preferable to limit the carbon content to 0.09 to 0.4%.
マンガン(Mn):0.3〜4.5%
マンガンは、硬化能を増加させることで鋼板の強度を向上させる元素である。かかる効果を得るために、その含有量が0.3%以上であることが好ましい。これに対し、4.5%を超えると、偏析層構造が原因で鋼板の成形性が低下するおそれがある。したがって、本発明のMnの含有量は、0.3〜4.5%に制限することが好ましい。
Manganese (Mn): 0.3-4.5%
Manganese is an element that improves the strength of the steel sheet by increasing the hardenability. In order to obtain such an effect, the content is preferably 0.3% or more. On the other hand, if it exceeds 4.5%, the formability of the steel sheet may be reduced due to the segregation layer structure. Therefore, the Mn content of the present invention is preferably limited to 0.3 to 4.5%.
上記クラッド材の残りの成分は鉄(Fe)である。但し、通常の製造過程では、原料や周囲の環境から意図しない不純物が必然的に混入される可能性があるため、これを排除することはできない。これらの不純物は、通常の製造過程における技術者であれば誰でも分かるものであるため、そのすべての内容を具体的に言及することはしない。 The remaining component of the cladding material is iron (Fe). However, in a normal manufacturing process, unintended impurities may be inevitably mixed from the raw materials and the surrounding environment, and thus cannot be excluded. Since these impurities can be understood by any engineer in the normal manufacturing process, the entire contents thereof are not specifically mentioned.
上記組成に加えて、クラッド材を構成するマルテンサイト系炭素鋼は、重量%で、Si:0.03〜1.0%、Al:0.02〜0.3%、N:0.04%以下(0%は除く)、B:0.0005〜0.005%、P:0.03%以下、及びS:0.03%以下をさらに含むことができる。 In addition to the above composition, the martensitic carbon steel constituting the clad material is, by weight, Si: 0.03-1.0%, Al: 0.02-0.3%, N: 0.04% The following may be included (excluding 0%), B: 0.0005 to 0.005%, P: 0.03% or less, and S: 0.03% or less.
シリコン(Si):0.03〜1.0%
シリコン(Si)は、鋼板内に固溶されて鋼の強度を向上させる役割を果たす。シリコンは、溶鋼中に不純物として存在する元素であって、0.03%未満に制御するためには過大な費用が発生する。これに対し、その含有量が1.0%を超えると、焼鈍の際に表面酸化物を生成し、鋼板の表面品質が劣化することがある。したがって、上記シリコンの含有量は、0.03〜1.0%であることが好ましい。
Silicon (Si): 0.03-1.0%
Silicon (Si) plays a role of improving the strength of steel by being dissolved in the steel plate. Silicon is an element present as an impurity in molten steel, and excessive costs are required to control it to less than 0.03%. On the other hand, when the content exceeds 1.0%, a surface oxide may be generated during annealing, and the surface quality of the steel sheet may deteriorate. Therefore, the silicon content is preferably 0.03 to 1.0%.
アルミニウム(Al):0.02〜0.3%
アルミニウムは、通常、脱酸のために添加する元素である。その含有量を0.02%未満に制御するためには過大な費用が発生し、その含有量が0.3%を超えると、焼鈍の際に表面酸化物を生成し、鋼板の表面品質が劣化することがある。したがって、上記アルミニウムの含有量は、0.02〜0.3%であることが好ましい。
Aluminum (Al): 0.02-0.3%
Aluminum is an element usually added for deoxidation. In order to control the content to less than 0.02%, an excessive cost is generated. When the content exceeds 0.3%, surface oxide is generated during annealing, and the surface quality of the steel sheet is reduced. May deteriorate. Therefore, the aluminum content is preferably 0.02 to 0.3%.
窒素(N):0.04%以下(0%は除く)
窒素(N)は、必然的に含有される元素であって、鋼中に残留するアルミニウムと反応して生成されたAlNは、連続鋳造の際に表面割れを生じさせることがある。したがって、その含有量をできる限り低く制御することが好ましいが、製造工程上必然的に含有される。窒素は上限を管理することが重要であり、本発明では、上記窒素の含有量の上限は0.04%に管理するとよい。
Nitrogen (N): 0.04% or less (excluding 0%)
Nitrogen (N) is an element that is inevitably contained, and AlN produced by reaction with aluminum remaining in the steel may cause surface cracks during continuous casting. Therefore, the content is preferably controlled as low as possible, but is inevitably contained in the production process. It is important to manage the upper limit of nitrogen. In the present invention, the upper limit of the nitrogen content is preferably controlled to 0.04%.
ホウ素(B):0.0005〜0.005%
ホウ素(B)は、オーステナイト結晶粒界に偏析して結晶粒界のエネルギーを低減する元素であり、鋼の硬化能を向上させる元素である。そのため、ホウ素は0.0005%以上含まれることが好ましいが、0.005%を超えると、表面に酸化物を形成して鋼板の表面品質が劣化することがある。したがって、上記ホウ素の含有量は、0.0005〜0.005%であることが好ましい。
Boron (B): 0.0005 to 0.005%
Boron (B) is an element that segregates at the austenite grain boundaries and reduces the energy of the grain boundaries, and is an element that improves the hardenability of the steel. Therefore, it is preferable that boron is contained in an amount of 0.0005% or more. However, if it exceeds 0.005%, an oxide may be formed on the surface to deteriorate the surface quality of the steel sheet. Therefore, the boron content is preferably 0.0005 to 0.005%.
リン(P):0.03%以下
上記リン(P)は、必然的に含まれる不純物であって、偏析によって鋼の加工性を低下させる主な原因となる元素であるため、その含有量を可能な限り低く制御することが好ましい。理論上リンの含有量は0%に制限することが有利であるが、製造工程上必然的に含有される。したがって、上限を管理することが重要であり、本発明では、上記リンの含有量の上限を0.03%に管理するとよい。
Phosphorus (P): 0.03% or less Phosphorus (P) is an impurity that is inevitably contained, and is an element that is a main cause of reducing the workability of steel by segregation. It is preferable to control as low as possible. Theoretically, the phosphorus content is advantageously limited to 0%, but is necessarily contained in the production process. Therefore, it is important to manage the upper limit, and in the present invention, the upper limit of the phosphorus content is preferably managed to 0.03%.
硫黄(S):0.03%以下
硫黄は、必然的に含まれる不純物であって、粗大なマンガン硫化物(MnS)を形成してフランジクラックなどの欠陥を発生させ、鋼板の穴拡げ性を大幅に低下させるため、その含有量を可能な限り低く制御することが好ましい。理論上硫黄の含有量は0%に制限することが有利であるが、製造工程上必然的に含有される。したがって、上限を管理することが重要であり、本発明では、上記硫黄の含有量の上限を0.03%に管理するとよい。
Sulfur (S): 0.03% or less Sulfur is an impurity that is inevitably contained, and forms coarse manganese sulfide (MnS) to generate defects such as flange cracks, thereby increasing the hole expandability of the steel sheet. In order to reduce significantly, it is preferable to control the content as low as possible. Theoretically, the sulfur content is advantageously limited to 0%, but is necessarily contained in the production process. Therefore, it is important to manage the upper limit, and in the present invention, the upper limit of the sulfur content is preferably managed to 0.03%.
また、上記組成に加えて、クラッド材を構成するマルテンサイト系炭素鋼は、重量%で、Cr:0.1〜1.0%、Ni:0.1〜1.0%、Mo:0.05〜1.0%、Ti:0.005〜0.05%、及びNb:0.005〜0.05%のうち1以上をさらに含むことができる。 Moreover, in addition to the said composition, the martensitic carbon steel which comprises a clad material is weight%, Cr: 0.1-1.0%, Ni: 0.1-1.0%, Mo: 0.00. It may further include one or more of 05 to 1.0%, Ti: 0.005 to 0.05%, and Nb: 0.005 to 0.05%.
クロム(Cr):0.1〜1.0%
クロムは、鋼の硬化能を向上させる元素であって、低温変態相の生成を促進することで鋼の強度を向上させる元素である。かかる効果を得るためには、その含有量が0.1%以上であることが好ましいが、その含有量が1.0%を超えると、意図する強度の向上効果に比べて過大な製造コストの増加を誘発することがある。したがって、上記クロムの含有量は、0.1〜1.0%であることが好ましい。
Chromium (Cr): 0.1-1.0%
Chromium is an element that improves the hardenability of the steel, and is an element that improves the strength of the steel by promoting the formation of a low-temperature transformation phase. In order to obtain such an effect, the content is preferably 0.1% or more. However, if the content exceeds 1.0%, the production cost is excessive compared with the intended effect of improving the strength. May induce an increase. Therefore, the chromium content is preferably 0.1 to 1.0%.
ニッケル(Ni):0.1〜1.0%
ニッケルは、鋼の硬化能を向上させるとともに、鋼の強度を向上させる元素である。かかる効果を得るためには、その含有量が0.1%以上であることが好ましいが、その含有量が1.0%を超えると、意図する強度の向上効果に比べて過大な製造コストの増加を誘発することがある。したがって、上記ニッケルの含有量は、0.1〜1.0%であることが好ましい。
Nickel (Ni): 0.1-1.0%
Nickel is an element that improves the hardenability of the steel and improves the strength of the steel. In order to obtain such an effect, the content is preferably 0.1% or more. However, if the content exceeds 1.0%, the production cost is excessive compared with the intended effect of improving the strength. May induce an increase. Therefore, the nickel content is preferably 0.1 to 1.0%.
モリブデン(Mo):0.05〜1.0%
モリブデンは、鋼の硬化能を向上させる元素であって、低温変態相の生成を促進して鋼の強度を向上させるとともに、鋼中に炭化物を形成して鋼の強度を向上させる元素である。かかる効果を得るためには、その含有量が0.05%以上であることが好ましいが、その含有量が1.0%を超えると、意図する強度の向上効果に比べて過大な製造コストの増加を誘発することがある。したがって、上記モリブデンの含有量は、0.01〜1.0%であることが好ましい。
Molybdenum (Mo): 0.05-1.0%
Molybdenum is an element that improves the hardenability of steel, promotes the formation of a low-temperature transformation phase to improve the strength of the steel, and forms carbides in the steel to improve the strength of the steel. In order to obtain such an effect, the content is preferably 0.05% or more. However, if the content exceeds 1.0%, the production cost is excessive compared to the intended effect of improving the strength. May induce an increase. Therefore, the molybdenum content is preferably 0.01 to 1.0%.
チタン(Ti):0.005〜0.05%
チタン(Ti)は0.005〜0.05%であることが好ましい。チタンは、鋼内部の窒素及び炭素と反応し、炭窒化物を形成して強度を増加させる役割を果たす。このために、チタンは0.005%以上含まれることが好ましいが、0.05%を超えると、沈殿物が大量に形成されて鋳造性を悪化させることがある。したがって、上記チタンの含有量は、0.005〜0.05%であることが好ましい。
Titanium (Ti): 0.005 to 0.05%
Titanium (Ti) is preferably 0.005 to 0.05%. Titanium reacts with nitrogen and carbon inside the steel to form carbonitrides and increase the strength. For this reason, titanium is preferably contained in an amount of 0.005% or more, but if it exceeds 0.05%, a large amount of precipitates may be formed, which may deteriorate castability. Therefore, the titanium content is preferably 0.005 to 0.05%.
ニオブ(Nb):0.005〜0.05%
ニオブ(Nb)は、0.005〜0.05%であることが好ましい。ニオブは、チタンのような炭窒化物形成元素として鋼材内部の窒素及び炭素と反応して強度を増加させる役割を果たす。このために、ニオブは0.005%以上含まれることが好ましいが、0.05%を超えると、沈殿物が大量に形成されて鋳造性を悪化させることがある。したがって、上記ニオブの含有量は、0.005〜0.05%であることが好ましい。
Niobium (Nb): 0.005 to 0.05%
Niobium (Nb) is preferably 0.005 to 0.05%. Niobium acts as a carbonitride-forming element such as titanium and reacts with nitrogen and carbon inside the steel material to increase the strength. For this reason, niobium is preferably contained in an amount of 0.005% or more, but if it exceeds 0.05%, a large amount of precipitates may be formed, which may deteriorate castability. Therefore, the niobium content is preferably 0.005 to 0.05%.
一方、本発明において、クラッド材を構成するマルテンサイト系炭素鋼は、上記成分系を満たすだけでなく、微細組織が、マルテンサイトが65面積%以上であり、残りは残留オーステナイト、フェライト、ベイナイト、及び炭化物のうち1以上からなることができる。上記のような微細組織を確保することにより、優れた引張強度及び降伏強度を確保することができる。 On the other hand, in the present invention, the martensitic carbon steel constituting the cladding material not only satisfies the above component system, but also has a fine structure of martensite of 65 area% or more, and the remainder is retained austenite, ferrite, bainite, And one or more of the carbides. By ensuring the fine structure as described above, excellent tensile strength and yield strength can be ensured.
また、焼戻し処理により、微細組織が、焼戻しマルテンサイトが65面積%以上であり、残りは残留オーステナイト、フェライト、ベイナイト、及び炭化物のうち1以上からなることができる。これは、焼戻し処理によるマルテンサイト変態を介して鋼内部に生成された残留応力を除去し、鋼の靭性を向上させるためである。 Further, the tempering treatment can be such that the microstructure is 65% by area or more of tempered martensite, and the remainder consists of one or more of retained austenite, ferrite, bainite, and carbide. This is for removing the residual stress produced | generated inside steel through the martensitic transformation by a tempering process, and improving the toughness of steel.
(クラッド鋼板)
本発明の一側面によるクラッド鋼板は、上述した母材と、上記母材の両側面に備えられるクラッド材と、を含む。
(Clad steel plate)
A clad steel plate according to one aspect of the present invention includes the above-described base material and a clad material provided on both side surfaces of the base material.
クラッド鋼板は、二つ以上の金属材料の表面を冶金学的に接合して一体化させた積層型複合材料として定義される。一般に、クラッド鋼板は、ニッケル(Ni)や銅(Cu)のような貴金属をクラッド材として用いることで、激しい腐食環境などの特殊な目的のために使用されてきた。 A clad steel plate is defined as a laminated composite material in which the surfaces of two or more metal materials are metallurgically joined together. In general, clad steel plates have been used for special purposes such as severe corrosive environments by using noble metals such as nickel (Ni) and copper (Cu) as clad materials.
本発明の内部鋼材である母材は、高合金量により強度及び伸びに優れたオーステナイト系高マンガン鋼である。オーステナイト系高マンガン鋼は、大量の合金成分が原因で製造コストが高くなり、900MPa以上の降伏強度を確保することが難しいため、耐衝突特性が要求される自動車構造部材として用いるのに不適である。 The base material which is the internal steel material of the present invention is an austenitic high manganese steel which is excellent in strength and elongation due to a high alloy amount. Austenitic high-manganese steel is unsuitable for use as an automobile structural member that requires high impact resistance because the production cost is high due to a large amount of alloy components and it is difficult to ensure a yield strength of 900 MPa or more. .
本発明の外部鋼材であるクラッド材は、降伏強度及び引張強度に優れたマルテンサイト系炭素鋼である。マルテンサイト系炭素鋼は、伸びが低く成形性を確保することが難しい。 The clad material which is the outer steel material of the present invention is a martensitic carbon steel excellent in yield strength and tensile strength. Martensitic carbon steel has low elongation and it is difficult to ensure formability.
マルテンサイト系鋼材は、成形の際に変形が局部的に集中して均一伸びが低いことが原因で成形性が劣化する特性を示す。一方、本発明者らは、内部に均一伸びが高いオーステナイト系高マンガン鋼を含むクラッド鋼板として製作されている場合、マルテンサイト系鋼材の局部的な変形集中が防止され、成形性が向上するという現象を見出した。 A martensitic steel material exhibits a characteristic that its formability deteriorates due to local concentration during deformation and low uniform elongation. On the other hand, when the present inventors are manufactured as a clad steel sheet containing austenitic high manganese steel with high uniform elongation inside, local deformation concentration of martensitic steel material is prevented and formability is improved. I found the phenomenon.
したがって、本発明では、上述したオーステナイト系高マンガン鋼を母材とし、母材の両側面に上述したマルテンサイト系炭素鋼をクラッド材として含ませることにより、それぞれの欠点を克服することができ、強度及び成形性がともに優れるようにするという効果を得ることができる。 Therefore, in the present invention, the above-mentioned austenitic high-manganese steel is used as a base material, and the above-described martensitic carbon steel is included as a clad material on both side surfaces of the base material, whereby each disadvantage can be overcome, It is possible to obtain an effect that both strength and formability are excellent.
この場合、上記母材の厚さは、上記クラッド鋼板の厚さの30〜90%であることができる。
上記母材の厚さが上記クラッド鋼板の厚さの90%を超える場合には、強度が低下し、製造コストが上昇するという問題点がある。これに対し、30%未満の場合には、クラッド鋼板の成形性が劣化するという問題がある。
In this case, the thickness of the base material may be 30 to 90% of the thickness of the clad steel plate.
When the thickness of the base material exceeds 90% of the thickness of the clad steel plate, there is a problem that the strength is lowered and the manufacturing cost is increased. On the other hand, when it is less than 30%, there is a problem that the formability of the clad steel plate deteriorates.
また、上記クラッド鋼板の厚さは、0.6〜30mmであることができ、より好ましくは1.0〜20mmであることができる。 Moreover, the thickness of the said clad steel plate can be 0.6-30 mm, More preferably, it can be 1.0-20 mm.
また、上記クラッド鋼板は、降伏強度が700MPa以上であり、好ましくは900MPa以上、引張強度と伸びの積が25,000MPa%以上であってもよい。かかる降伏強度、引張強度、及び伸びを確保することにより、自動車構造部材などに好適に適用されることができる。 The clad steel sheet may have a yield strength of 700 MPa or more, preferably 900 MPa or more, and a product of tensile strength and elongation of 25,000 MPa% or more. By securing such yield strength, tensile strength, and elongation, it can be suitably applied to automobile structural members and the like.
一方、上記クラッド鋼板はめっき層をさらに含むことができる。上記めっき層は、Zn系、Zn−Fe系、Zn−Al系、Zn−Mg系、Zn−Mg−Al系、Zn−Ni系、Al−Si系、及びAl−Si−Mg系からなる群より選択された1種であってもよい。 Meanwhile, the clad steel plate may further include a plating layer. The plating layer is made of Zn, Zn-Fe, Zn-Al, Zn-Mg, Zn-Mg-Al, Zn-Ni, Al-Si, and Al-Si-Mg. It may be one more selected.
「強度及び成形性に優れたクラッド鋼板の製造方法」
以下、本発明の他の一側面による強度及び成形性に優れたクラッド鋼板の製造方法について詳細に説明する。
"Production method of clad steel sheet with excellent strength and formability"
Hereinafter, a method for producing a clad steel sheet excellent in strength and formability according to another aspect of the present invention will be described in detail.
本発明の他の一側面による強度及び成形性に優れたクラッド鋼板の製造方法は、上述した合金組成を満たすオーステナイト系高マンガン鋼の母材を用意する段階と、上述した合金組成を満たすマルテンサイト系炭素鋼のクラッド材を用意する段階と、二つの上記クラッド材の間に上記母材を配置して積層物を得る段階と、上記積層物の端を溶接した後、1050〜1350℃の温度範囲で加熱する段階と、上記加熱された積層物を750〜1050℃の温度範囲で仕上げ圧延して熱延鋼板を得る段階と、上記熱延鋼板を50〜700℃で巻取る段階と、上記巻取られた熱延鋼板を酸洗した後、冷間圧下率35〜90%を適用して冷間圧延することで冷延鋼板を得る段階と、上記冷間圧延鋼板を550℃以上上記クラッド材のA3+200℃以下の温度範囲で焼鈍する段階と、を含む。 According to another aspect of the present invention, a method for manufacturing a clad steel sheet excellent in strength and formability includes a step of preparing a base material of an austenitic high manganese steel that satisfies the above-described alloy composition, and martensite that satisfies the above-described alloy composition. A step of preparing a clad material of a carbon steel, a step of arranging the base material between two clad materials to obtain a laminate, and welding the ends of the laminate, followed by a temperature of 1050 to 1350 ° C. Heating in a range, finishing rolling the heated laminate in a temperature range of 750 to 1050 ° C. to obtain a hot-rolled steel plate, winding the hot-rolled steel plate at 50 to 700 ° C., and After pickling the wound hot-rolled steel sheet, applying a cold reduction ratio of 35 to 90% and cold rolling to obtain a cold-rolled steel sheet; and A3 + 200 ℃ or higher Comprising of the steps of annealing in the temperature range, the.
(母材とクラッドの用意段階及び積層段階)
上述した合金組成を満たす母材とクラッド材を用意した後、二つの上記クラッド材の間に上記母材を配置して積層物を得る。この場合、積層前の母材及びクラッド材の表面を洗浄することができる。
(Preparation and lamination stages of base material and cladding)
After preparing a base material and a clad material that satisfy the alloy composition described above, the base material is placed between the two clad materials to obtain a laminate. In this case, the surface of the base material and the clad material before lamination can be cleaned.
ここで、上記母材及びクラッド材はスラブの形であることができ、上記母材及びクラッド材の製造方法は、一般の製造工程を適用して生産することができるため、特に限定されない。但し、好ましい一例として、上記母材は、電気炉又は高炉で生産された溶鋼を鋳造してスラブとなるように製造されることができ、上記クラッド材は、高炉で生産された溶鋼を精錬及び鋳造して、不可避に含有される可能性がある不純物の含有量を制御してスラブとなるように製造されることができる。 Here, the base material and the clad material may be in the form of a slab, and the manufacturing method of the base material and the clad material is not particularly limited because it can be produced by applying a general manufacturing process. However, as a preferable example, the base material can be manufactured so as to be a slab by casting molten steel produced in an electric furnace or blast furnace, and the clad material is refined and refined from molten steel produced in a blast furnace. The slab can be manufactured by controlling the content of impurities that may be inevitably contained by casting.
(溶接及び加熱段階)
上記積層物の端を溶接した後、1050〜1350℃の温度範囲で加熱する。
積層物の端を溶接することにより、母材とクラッド材の間に酸素が侵入することを防止することができ、加熱時の酸化物の生成を防止することができる。
上記加熱温度が1050℃未満の場合には、熱間圧延時の仕上げ圧延温度を確保することが難しく、温度減少によって圧延荷重が増加し、所定の厚さまで十分に圧延することが難しくなるという問題がある。これに対し、加熱温度が1350℃を超えると、結晶粒度が増加し、表面酸化が発生して、強度が低下するか、又は表面が劣化するという傾向があるため好ましくない。また、連続鋳造スラブの柱状晶粒界に液状膜が生成されるため、後続の熱間圧延時に割れが発生するおそれがある。
(Welding and heating stage)
After the end of the laminate is welded, it is heated in a temperature range of 1050 to 1350 ° C.
By welding the end of the laminate, oxygen can be prevented from entering between the base material and the clad material, and the formation of oxides during heating can be prevented.
When the heating temperature is less than 1050 ° C., it is difficult to ensure the finish rolling temperature during hot rolling, the rolling load increases due to the temperature decrease, and it is difficult to sufficiently roll to a predetermined thickness. There is. On the other hand, if the heating temperature exceeds 1350 ° C., the crystal grain size increases, surface oxidation occurs, the strength tends to decrease, or the surface tends to deteriorate, such being undesirable. Further, since a liquid film is generated at the columnar grain boundaries of the continuously cast slab, there is a possibility that cracks may occur during subsequent hot rolling.
(熱間圧延段階)
上記加熱された積層物を750〜1050℃の温度範囲で仕上げ圧延して熱延鋼板を得る。
上記仕上げ圧延温度が750℃未満の場合には、圧延荷重が高くなり、圧延機に負担がかかるという問題がある。一方、仕上げ圧延温度が1050℃を超えると、圧延の際に表面酸化が発生するおそれがある。
(Hot rolling stage)
The heated laminate is finish-rolled in a temperature range of 750 to 1050 ° C. to obtain a hot-rolled steel sheet.
When the finish rolling temperature is less than 750 ° C., there is a problem that the rolling load becomes high and a burden is imposed on the rolling mill. On the other hand, if the finish rolling temperature exceeds 1050 ° C., surface oxidation may occur during rolling.
(巻取段階)
上記熱延鋼板を50〜700℃で巻取りする。巻取温度が50℃未満の場合には、鋼板の温度を低下させるために、冷却水噴射による冷却が必要となり、不要な工程費用の上昇を誘発する。これに対し、巻取温度が700℃を超えると、熱延鋼板の表面に厚い酸化膜が生成されるようになる。これは、酸洗過程で酸化層の制御が容易でなくなるという問題をもたらしうる。したがって、上記巻取温度は50〜700℃に制限することが好ましい。
(Winding stage)
The hot rolled steel sheet is wound up at 50 to 700 ° C. When the coiling temperature is less than 50 ° C., cooling by cooling water injection is necessary to lower the temperature of the steel sheet, and an unnecessary process cost is increased. On the other hand, when the coiling temperature exceeds 700 ° C., a thick oxide film is generated on the surface of the hot rolled steel sheet. This can lead to a problem that the oxide layer cannot be easily controlled during the pickling process. Therefore, the winding temperature is preferably limited to 50 to 700 ° C.
(冷間圧延段階)
上記巻取られた熱延鋼板を酸洗した後、冷間圧下率35〜90%を適用して冷間圧延することで冷延鋼板を得る。
上記冷間圧下率が30%未満の場合には、クラッド材を構成するマルテンサイト炭素鋼の再結晶が円滑に行われず、加工性が劣化するという問題がある。これに対し、冷間圧下率が90%を超えると、圧延負荷によって板破断の発生可能性が高くなるという問題がある。
(Cold rolling stage)
The picked hot-rolled steel sheet is pickled and then cold-rolled by applying a cold reduction rate of 35 to 90% to obtain a cold-rolled steel sheet.
When the cold rolling reduction is less than 30%, there is a problem that the martensitic carbon steel constituting the clad material is not recrystallized smoothly and the workability is deteriorated. On the other hand, when the cold rolling reduction exceeds 90%, there is a problem that the possibility of plate breakage increases due to the rolling load.
(焼鈍段階)
上記冷延鋼板を550℃以上上記クラッド材のA3+200℃以下で焼鈍する。これは、強度及び再結晶により加工性を確保するためである。
焼鈍温度が550℃未満の場合には、母材であるオーステナイト系高マンガン鋼の再結晶が起こらないため十分な加工性を確保することができない。これに対し、上記クラッド材のA3+200℃を超える温度で焼鈍する場合には、クラッド材の結晶粒度が粗大となるため、鋼の強度を低下させる可能性がある。
したがって、焼鈍温度は、550℃〜上記クラッド材のA3+200℃の温度範囲で行うことが好ましい。
(Annealing stage)
The cold-rolled steel sheet is annealed at 550 ° C. or higher and A3 + 200 ° C. or lower of the clad material. This is to ensure workability by strength and recrystallization.
When the annealing temperature is less than 550 ° C., sufficient workability cannot be ensured because recrystallization of the austenitic high manganese steel as a base material does not occur. On the other hand, when annealing at a temperature exceeding A3 + 200 ° C. of the clad material, the crystal grain size of the clad material becomes coarse, which may reduce the strength of the steel.
Therefore, the annealing temperature is preferably performed in a temperature range of 550 ° C. to A3 + 200 ° C. of the cladding material.
この場合、上記焼鈍後の冷却速度は5℃/s以上であることができる。5℃/s未満の場合には、クラッド材のマルテンサイト分率を65面積%以上に確保することが難しくなる。 In this case, the cooling rate after the annealing can be 5 ° C./s or more. When it is less than 5 ° C./s, it becomes difficult to ensure the martensite fraction of the clad material to 65 area% or more.
また、上記焼鈍された冷延鋼板をMs(マルテンサイト変態開始温度)以下に冷却した後、A1以下の温度で加熱して焼戻しする段階をさらに含むことができる。 In addition, the method may further include a step of cooling the annealed cold-rolled steel sheet to Ms (martensite transformation start temperature) or lower and then heating and tempering at a temperature of A1 or lower.
一方、上記焼鈍する段階後に、めっきしてめっき層を形成する段階をさらに含むことができる。ここで、上記めっき層は、Zn系、Zn−Fe系、Zn−Al系、Zn−Mg系、Zn−Mg−Al系、Zn−Ni系、Al−Si系、及びAl−Si−Mg系からなる群より選択された1種であってもよい。 Meanwhile, the method may further include forming a plating layer by plating after the annealing step. Here, the plating layer is made of Zn, Zn—Fe, Zn—Al, Zn—Mg, Zn—Mg—Al, Zn—Ni, Al—Si, and Al—Si—Mg. It may be one selected from the group consisting of
以下、実施例を通じて本発明をより具体的に説明する。但し、下記実施例は本発明を例示してより詳細に説明するためのもので、本発明の権利範囲を限定するためのものではないことに留意する必要がある。本発明の権利範囲は、特許請求の範囲に記載された事項及びこれから合理的に類推される事項によって決定されるためである。 Hereinafter, the present invention will be described in more detail through examples. However, it should be noted that the following examples are for illustrating the present invention in more detail and are not intended to limit the scope of rights of the present invention. This is because the scope of rights of the present invention is determined by matters described in the claims and matters reasonably inferred therefrom.
下記表1に示す成分組成を有するオーステナイト系高マンガン鋼(A1〜A4)、マルテンサイト系炭素鋼(B1〜B4)、及び極低炭素鋼(C)の鋼塊を用意し、1150℃の加熱炉で1時間再加熱した後、900℃の仕上げ圧延温度で圧延して熱延鋼板を製造した。その後、上記熱延鋼板を450℃で巻取った後、酸洗後に、50%の冷間圧下率で冷間圧延して冷延鋼板を製造した。次に、下記表2に記載された焼鈍温度で焼鈍した後、下記表2に記載された冷却速度で常温まで冷却した。製造されたそれぞれの試験片に対して、万能引張実験機を用いて引張試験を行うことで、降伏強度(YS)、引張強度(TS)、及び伸び(EL)を測定し、下記表2に示した。また、光学顕微鏡で微細組織を観察して微細組織を構成する各相の面積分率を下記表2に示した。
クラッド鋼板でなく、マルテンサイト系炭素鋼(B1〜B4)単独では伸びが劣化し、オーステナイト系高マンガン鋼(A1〜A4)単独では高い降伏強度及び引張強度を確保することに限界があることが下記表2から確認できる。
Austenitic high manganese steel (A1 to A4), martensitic carbon steel (B1 to B4), and ultra low carbon steel (C) ingots having the composition shown in Table 1 below are prepared, and heated at 1150 ° C. After reheating in a furnace for 1 hour, a hot rolled steel sheet was manufactured by rolling at a finish rolling temperature of 900 ° C. Thereafter, the hot-rolled steel sheet was wound at 450 ° C. and then pickled and then cold-rolled at a cold reduction of 50% to produce a cold-rolled steel sheet. Next, after annealing at the annealing temperature described in Table 2 below, it was cooled to room temperature at the cooling rate described in Table 2 below. Yield strength (YS), tensile strength (TS), and elongation (EL) are measured by performing a tensile test on each manufactured test piece using a universal tensile testing machine. Indicated. In addition, Table 2 below shows the area fraction of each phase constituting the microstructure by observing the microstructure with an optical microscope.
The martensitic carbon steel (B1 to B4) alone is not a clad steel plate, but the elongation deteriorates, and the austenitic high manganese steel (A1 to A4) alone has a limit in securing high yield strength and tensile strength. It can be confirmed from Table 2 below.
一方、下記表1に示す成分組成を有するオーステナイト系高マンガン鋼(A1〜A4)、マルテンサイト系炭素鋼(B1〜B4)、及び極低炭素鋼(C)の鋼塊を用意し、鋼塊の表面を洗浄した後、2つの炭素鋼の間に高マンガン鋼を配置して下記表3の積層比を有するように3重積層物を作製した。次に、積層物の境界面に沿って溶接棒を用いてアーク溶接した。上記境界面が溶接された積層物を1150℃の加熱炉で1時間加熱した後、900℃の仕上げ圧延温度で圧延して熱延鋼板を製造した。その後、上記熱延鋼板を450℃で巻取った後、酸洗後に、50%の冷間圧下率で冷間圧延して冷延鋼板を製造した。続いて、下記表3に記載された焼鈍温度で焼鈍した後、下記表3に記載された冷却速度で常温まで冷却した。製造されたそれぞれの試験片に対して、万能引張実験機を用いて引張試験を行うことで、降伏強度(YS)、引張強度(TS)、伸び(EL)、及びTS×ELの値を測定して下記表3に示した。 On the other hand, steel ingots of austenitic high manganese steel (A1 to A4), martensitic carbon steel (B1 to B4), and extremely low carbon steel (C) having the composition shown in Table 1 below are prepared. After cleaning the surface, a high-manganese steel was placed between two carbon steels to prepare a triple laminate having the lamination ratio shown in Table 3 below. Next, arc welding was performed using a welding rod along the boundary surface of the laminate. The laminate with the boundary surface welded was heated in a 1150 ° C. heating furnace for 1 hour, and then rolled at a finish rolling temperature of 900 ° C. to produce a hot-rolled steel sheet. Thereafter, the hot-rolled steel sheet was wound at 450 ° C. and then pickled and then cold-rolled at a cold reduction of 50% to produce a cold-rolled steel sheet. Then, after annealing at the annealing temperature described in the following Table 3, it was cooled to room temperature at the cooling rate described in the following Table 3. The yield strength (YS), tensile strength (TS), elongation (EL), and TS × EL values are measured by performing a tensile test on each manufactured specimen using a universal tensile testing machine. The results are shown in Table 3 below.
本発明の組成及び微細組織をともに満たす発明例1〜発明例41は、700MPa以上の降伏強度、及び引張強度と伸びの積が25,000MPa%以上を確保できることが確認できる。 It can be confirmed that Invention Examples 1 to 41 satisfying both the composition and microstructure of the present invention can secure a yield strength of 700 MPa or more and a product of tensile strength and elongation of 25,000 MPa% or more.
これに対し、比較例1の場合、本発明で提示する母材とクラッド材の厚さ比は満たしているものの、母材の微細組織がフェライト単相からなることから、700MPa以上の降伏強度、及び25,000MPa%以上の引張強度と伸びの積を確保することはできなかった。 On the other hand, in the case of Comparative Example 1, although the thickness ratio of the base material and the clad material presented in the present invention is satisfied, since the microstructure of the base material is composed of a ferrite single phase, a yield strength of 700 MPa or more, And the product of tensile strength and elongation of 25,000 MPa% or more could not be ensured.
一方、比較例2の場合、本発明で提示する母材とクラッド材の厚さ比は満たしているものの、クラッドの微細組織がフェライト単相からなることから、700MPa以上の降伏強度、及び25,000MPa%以上の引張強度と伸びの積を確保することができなかった。 On the other hand, in the case of Comparative Example 2, although the thickness ratio of the base material and the clad material presented in the present invention is satisfied, since the clad microstructure is composed of a single phase of ferrite, a yield strength of 700 MPa or more and 25, A product of tensile strength and elongation of 000 MPa% or more could not be secured.
また、比較例3の場合、母材とクラッド材の微細組織は本発明で提示する条件を満たしているものの、母材の厚さ比が30%以下で製作されて、700MPa以上の降伏強度又は25,000MPa%以上の引張強度と伸びの積を確保することができなかった。 In the case of Comparative Example 3, the microstructure of the base material and the clad material satisfies the conditions presented in the present invention, but the base material is manufactured with a thickness ratio of 30% or less, and has a yield strength of 700 MPa or more. A product of tensile strength and elongation of 25,000 MPa% or more could not be secured.
図1は、オーステナイト系高マンガン鋼を母材2とし、マルテンサイト系炭素鋼をクラッド材1及び3とするクラッド鋼板の模式図である。 FIG. 1 is a schematic view of a clad steel plate having an austenitic high manganese steel as a base material 2 and martensitic carbon steel as clad materials 1 and 3.
図2は、発明例1の断面を走査電子顕微鏡で撮影した写真であって、a)は1500倍率、b)は8000倍率で撮影した。界面を境にして、母材である高マンガン鋼は再結晶が完了し、均一な微細組織を有することが確認でき、クラッド材である炭素鋼は、マルテンサイト鋼特有の針状組織が発達することが分かる。母材とクラッド材の界面に酸化物の存在は発見されておらず、これにより、界面結合力が確保されて、加工時の界面分離による破断が発生しなかった。 FIG. 2 is a photograph of the cross section of Invention Example 1 taken with a scanning electron microscope, a) taken at 1500 magnifications, and b) taken at 8000 magnifications. At the interface, the high-manganese steel, which is the base material, has been recrystallized, and it can be confirmed that it has a uniform microstructure. The carbon steel, which is the clad material, develops a needle-like structure unique to martensite steel. I understand that. The presence of oxides at the interface between the base material and the clad material has not been found, thereby ensuring the interfacial bonding force and preventing breakage due to interfacial separation during processing.
図3は、表1のオーステナイト系高マンガン鋼(A1〜A4)、マルテンサイト系炭素鋼(B1〜B4)、及び表3の発明例1〜41の引張強度と伸びを示すグラフである。母材である高マンガン鋼及びクラッド材であるマルテンサイト系鋼の合金組成、微細組織、及び厚さ比を調節することにより、様々な引張強度及び伸びを有する鋼材を製造できることが確認できる。また、本発明による鋼材の降伏強度及び成形性に優れており、引張強度と伸びの積が25,000MPa%以上である自動車用の構造部材に適したクラッドを製造できることが確認できる。 FIG. 3 is a graph showing the tensile strength and elongation of austenitic high manganese steel (A1 to A4), martensitic carbon steel (B1 to B4) in Table 1, and Invention Examples 1 to 41 in Table 3. It can be confirmed that steel materials having various tensile strengths and elongations can be produced by adjusting the alloy composition, microstructure and thickness ratio of the high manganese steel as the base material and the martensitic steel as the clad material. Further, it can be confirmed that the steel material according to the present invention is excellent in yield strength and formability, and can produce a clad suitable for a structural member for an automobile having a product of tensile strength and elongation of 25,000 MPa% or more.
以上、実施例を参照して説明したが、当該技術分野の熟練した当業者は、添付の特許請求の範囲に記載された本発明の思想及び領域から逸脱しない範囲内で、本発明を多様に修正及び変更することができることを理解できる。 Although the present invention has been described with reference to the embodiments, those skilled in the art can make various changes to the present invention without departing from the spirit and scope of the present invention described in the appended claims. It can be understood that modifications and changes can be made.
Claims (21)
前記母材は、重量%で、C:0.3〜1.4%、Mn:12〜25%、残部Fe及び不可避不純物を含むオーステナイト系高マンガン鋼であり、
前記クラッド材は、重量%で、C:0.09〜0.4%、Mn:0.3〜4.5%、残部Fe及び不可避不純物を含むマルテンサイト系炭素鋼である、強度及び成形性に優れたクラッド鋼板。 A base material, and a clad material provided on both side surfaces of the base material,
The base material is austenitic high manganese steel containing C: 0.3 to 1.4%, Mn: 12 to 25%, the balance Fe and inevitable impurities in weight%,
The clad material is martensitic carbon steel containing C: 0.09 to 0.4%, Mn: 0.3 to 4.5%, balance Fe and unavoidable impurities in weight%, strength and formability Excellent clad steel plate.
重量%で、C:0.09〜0.4%、Mn:0.3〜4.5%、残部Fe及び不可避不純物を含むマルテンサイト系炭素鋼のクラッド材を用意する段階と、
二つの前記クラッド材の間に前記母材を配置して積層物を得る段階と、
前記積層物の端を溶接した後、1050〜1350℃の温度範囲で加熱する段階と、
前記加熱された積層物を750〜1050℃の温度範囲で仕上げ圧延して熱延鋼板を得る段階と、
前記熱延鋼板を50〜700℃で巻取る段階と、
前記巻取られた熱延鋼板を酸洗した後、冷間圧下率35〜90%を適用して冷間圧延することで冷延鋼板を得る段階と、
前記冷延鋼板を550℃以上前記クラッド材のA3+200℃以下の温度範囲で焼鈍する段階と、を含む、強度及び成形性に優れたクラッド鋼板の製造方法。 Preparing a base material of austenitic high manganese steel containing C: 0.3-1.4%, Mn: 12-25%, balance Fe and unavoidable impurities in weight%;
Providing a clad material of martensitic carbon steel containing C: 0.09 to 0.4%, Mn: 0.3 to 4.5%, balance Fe and inevitable impurities in weight%;
Arranging the base material between two clad materials to obtain a laminate;
After welding the ends of the laminate, heating in a temperature range of 1050 to 1350 ° C .;
Finishing and rolling the heated laminate in a temperature range of 750 to 1050 ° C. to obtain a hot-rolled steel sheet;
Winding the hot-rolled steel sheet at 50 to 700 ° C .;
After pickling the wound hot-rolled steel sheet, obtaining a cold-rolled steel sheet by cold rolling by applying a cold reduction rate of 35 to 90%;
Annealing the cold-rolled steel sheet in a temperature range of 550 ° C. or more and A3 + 200 ° C. or less of the clad material, and a method for producing a clad steel sheet having excellent strength and formability.
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